JP2017145469A - Manufacturing method of high strength steel sheet - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a manufacturing method of a steel sheet having high strength and excellent ductility and extension flange, without performing rapid cooling immediately after the hot rolling.SOLUTION: A method of manufacturing a high strength steel sheet having a metallographic structure including martensite as a primary phase and polygonal ferrite and residual austenite as a secondary phase includes a hot rolling step in which a slab having a predetermined chemical composition is wound at 650°C or lower after applying hot rolling in which rolling is completed from an Arpoint to 1100°C, a primary annealing step in which at (Acpoint-50°C) to (Acpoint-2°C), the hot roll steel sheet is kept for a time satisfying [1.4×10×exp{26500/(T+273)}≤t≤4.0×10], and a secondary annealing step in which after holding the annealed steel sheet for (Acpoint-40°C)or higher and lower than (Acpoint+100°C), followed by cooling to (Ms-200°C) to (Ms-20°C) such that an average cooling speed between 650 to 500°C becomes 15°C/s or larger, followed by holding for 100 seconds or shorter, further followed by cooling to 500°C to Ms point, still further followed by holding there for 30 seconds or longer.SELECTED DRAWING: None

Description

  The present invention relates to a method for producing a high-strength steel sheet, and more particularly to a method for producing a high-strength steel sheet having excellent ductility and stretch flangeability.

  In recent years, from the viewpoint of protecting the global environment, we are working to reduce carbon dioxide emissions in many fields. Automakers are also actively developing technology to reduce vehicle weight for the purpose of reducing fuel consumption. However, it is not easy to reduce the weight of the vehicle body because the emphasis is also placed on improving the anti-collision characteristics in order to ensure passenger safety.

  Therefore, in order to achieve both weight reduction of the vehicle body and impact resistance, it has been studied to reduce the thickness of the member using a high-strength steel plate. For this reason, a steel sheet having both high strength and excellent formability is strongly desired, and several techniques have been proposed so far in order to meet these requirements.

  For example, Patent Document 1 discloses a high-strength automobile having excellent impact safety and formability in which residual austenite having an average crystal grain size of 5 μm or less is dispersed in ferrite having an average crystal grain size of 10 μm or less. A steel sheet is disclosed.

  Patent Document 2 discloses a high-strength steel sheet excellent in elongation and stretch flangeability in which a second phase composed of retained austenite and / or martensite is finely dispersed in crystal grains.

  Patent Document 3 has an area ratio of 75% or more of ferrite phase, 1% or more of bainitic ferrite phase, and 1% or more and 10% or less of pearlite phase, and the martensite phase has an area ratio of 10 % Of martensite area ratio / (bainitic ferrite area ratio + pearlite area ratio) ≦ 0.6, and the ratio of the Mn concentration in the ferrite phase to the Mn concentration in the second phase is 0. A high-strength hot-dip galvanized steel sheet excellent in workability and impact resistance characteristics of 70 or more is disclosed.

Patent Document 4 has a two-phase structure composed of tempered martensite having an area ratio of 5% or more and 95% or less and the balance composed of ferrite, and the average Mn concentration C _{Mn · α} in the ferrite and the tempered martensite in the tempered martensite. A high-strength cold-rolled steel sheet excellent in the balance between elongation and stretch flangeability is disclosed, in which the ratio C _{Mn · α} / C _{Mn · M} to the average Mn concentration C _{Mn · M} is 0.95 or more.

  In Patent Document 5, after completion of hot rolling, after cooling to a temperature range of 720 ° C. or less within 1 second, and staying in a temperature range of more than 500 ° C. and 720 ° C. or less with a stay time of 1 second or more and 20 seconds or less A method for producing a high-strength hot-rolled steel sheet having good ductility and stretch flangeability, which is wound in a temperature range of 350 ° C. or higher and 500 ° C. or lower is disclosed.

Patent Document 6 discloses that after completion of hot rolling, the steel sheet is cooled to a temperature range of 780 ° C. or less within 0.4 seconds, wound, and subjected to cold rolling (Ac ₃ points−40 ° C.) or more. A method for producing a cold-rolled steel sheet having good ductility and stretch flangeability is disclosed in which the steel sheet is subjected to soaking treatment, cooled to a temperature range of 500 ° C. or lower and 300 ° C. or higher, and held in the temperature range for 30 seconds or longer. .

JP-A-11-61326 JP 2005-179703 A International Publication No. 2011/090179 JP 2010-156032 A JP 2012-251200 A International Publication No. 2013/005714

  In general, a steel sheet containing retained austenite in the metal structure exhibits a large elongation due to the effect of transformation-induced plasticity (TRIP) caused by martensitic transformation of retained austenite during processing, but due to the formation of hard martensite, Expandability is impaired. The steel sheet described in Patent Document 1 is said to have improved ductility and hole expandability by refining ferrite and retained austenite, but the hole expansion ratio is at most 1.5 and has sufficient press formability. It ’s not good. Further, in order to improve the work hardening index and improve the collision resistance safety, the main phase needs to be a soft ferrite phase, and it is difficult to obtain a high tensile strength.

  Moreover, in the technique described in Patent Document 2, in order to refine the second phase to a nano size and disperse it in the crystal grains, a large amount of expensive elements such as Cu and Ni are contained, and further, at a high temperature for a long time. It is necessary to perform a solution treatment, and the increase in manufacturing cost and the decrease in productivity are remarkable.

  Furthermore, according to Patent Document 3, the distribution of Mn in steel is made uniform, and the ratio of the Mn concentration in the ferrite phase to the Mn concentration in the second phase is 0.70 or more. Even if it is not introduced, the absorbed energy up to a low strain range of about 5% is large, and it is possible to improve the collision resistance. However, the main phase needs to be a soft ferrite phase, and it is difficult to obtain high tensile strength.

  And according to patent document 4, the difference of the hardness of a ferrite and a martensite becomes small by making ratio of the Mn density | concentration in a ferrite and a martensite or more into a fixed value or more, and in the interface of a ferrite and a martensite By reducing the stress concentration, it is said that a good stretch flangeability can be obtained with a tensile strength exceeding 1000 MPa. However, the strength-ductility balance (TS × EL) is less than 16000 MPa ·%, and it is difficult to apply to members that require ductility.

  By the way, because there are various processing modes for automobile parts, the required formability differs depending on the applied member, but ductility and stretch flangeability are positioned as important indicators of formability, It is desirable to combine these at a high level. Furthermore, in recent years, it is desired to have higher strength than before.

  The techniques disclosed in Patent Document 5 and Patent Document 6 described above are excellent techniques that meet such demands, but facilities that perform rapid cooling immediately after hot rolling are indispensable. Furthermore, since rapid cooling at several hundred degrees Celsius / second or more is continued to a temperature in the vicinity of 700 degrees Celsius, there is a problem that it is difficult to control the temperature of the steel sheet.

  The present invention has been made to solve the above-described problems, and has a high strength and a method for producing a steel sheet having excellent ductility and stretch flangeability without performing rapid cooling immediately after hot rolling. The purpose is to provide.

  As a result of intensive studies on the chemical composition of a high-strength steel sheet and the relationship between the steel structure and mechanical properties, the present inventors have obtained the following knowledge.

  (A) The steel structure is preferably hard to obtain high strength, and the steel structure is preferably homogeneous to obtain excellent stretch flangeability. Therefore, in order to combine high strength and excellent stretch flangeability, martensite which is a hard and homogeneous structure is suitable, and it is important to have a steel structure mainly composed of martensite.

  (B) Martensite is a structure with poor ductility. For this reason, it is difficult to ensure ductility simply by using a steel structure mainly composed of martensite.

  (C) By containing retained austenite in the steel structure, ductility is improved by the TRIP effect. However, when the retained austenite is coarse, coarse voids are formed by martensite generated by the processing-induced transformation, and the stretch flangeability deteriorates. In order to maintain stretch flangeability and improve ductility, it is effective to contain fine retained austenite and to make fine martensite caused by processing-induced transformation to suppress the formation of coarse voids. .

  (D) Fine retained austenite has high stability against deformation due to three-dimensional restraint from surrounding crystal grains. Therefore, high-strength steel sheet undergoes local deformation before the TRIP effect is fully manifested, improving ductility. May not be possible.

  (E) In order to improve the ductility of a high-strength steel sheet, it is effective to increase the work hardening index at the initial stage of deformation by adding soft polygonal ferrite, but in addition to the content of polygonal ferrite, polygonal ferrite It is possible to improve ductility while maintaining stretch flangeability by controlling the average particle size of each of these and the ratio of Mn concentration in martensite and polygonal ferrite to an appropriate range. The average grain size of polygonal ferrite contributes to the strengthening of polygonal ferrite by grain boundary strengthening, and the Mn concentration by solid solution strengthening, so these are controlled to an appropriate range, and the hardness difference between martensite and polygonal ferrite By controlling the above, it becomes possible to combine high strength, ductility and stretch flangeability at a high level.

(F) By subjecting the steel sheet to soaking for a predetermined time in a temperature range of (Ac ₃ points-50 ° C.) to (Ac ₃ points-2 ° C.), distribution of Mn occurs between ferrite and austenite. Subsequently, by performing the second annealing, it is possible to appropriately control the area ratio, particle size, and Mn concentration of martensite, polygonal ferrite and retained austenite. As a result, a steel sheet having high strength and excellent ductility and stretch flangeability can be obtained without performing rapid cooling immediately after hot rolling.

  The present invention has been made on the basis of the above findings, and the gist thereof is the following method for producing a high-strength steel sheet.

(1) A method for producing a high-strength steel sheet having a main phase of martensite and a metal structure containing polygonal ferrite and retained austenite in the second phase,
The manufacturing method of a high strength steel plate provided with the following process (A)-(C).
(A) In mass%,
C: 0.04% or more and less than 0.50%,
Si: 0.10% or more and less than 3.0%,
Mn: 1.5 to 8.0%,
P: 0.10% or less,
S: 0.030% or less,
sol. Al: 0.01 to 2.0%,
N: 0.010% or less,
Ti: 0 to 0.20%,
Nb: 0 to 0.10%,
V: 0 to 0.50%,
Cr: 0% or more and less than 1.0%,
Mo: 0 to 0.50%,
Ni: 0 to 1.0%,
B: 0 to 0.0050%,
Ca: 0 to 0.020%,
Mg: 0 to 0.020%,
REM: 0 to 0.020%,
Cu: 0 to 1.0%
Bi: 0 to 0.020%,
Balance: Fe and impurities,
For a slab having a chemical composition satisfying the following formula (i):
A hot rolling step in which hot rolling is performed in a temperature range of Ar _{3 to} 1100 ° C. to form a hot-rolled steel sheet, and winding is performed in a temperature range of 650 ° C. or lower.
0.5 ≦ Si + sol. Al ≦ 3.0 (i)
However, each element symbol in the above formula (i) represents the content (% by mass) of each element contained in the steel sheet.
(B) Primary holding the hot-rolled steel sheet obtained in the step (A) in a temperature range of (Ac ₃ points-50 ° C.) to (Ac ₃ points-2 ° C.) for a time satisfying the following formula (ii). Annealing process.
1.4 × 10 ⁻⁸ × exp {26500 / (T + 273)} ≦ t ≦ 4.0 × 10 ⁵ (ii)
However, the meaning of each symbol in the above formula (ii) is as follows.
t: Primary annealing holding time (seconds)
T: Primary annealing temperature (° C)
(C) After holding the annealed steel sheet obtained in the step (B) in a temperature range of (Ac ₃ points−40 ° C.) or more and less than (Ac ₃ points + 100 ° C.), the average in the temperature range of 650 to 500 ° C. After cooling to a temperature range of (Ms−200 ° C.) to (Ms−20 ° C.) so that the cooling rate is 15 ° C./second or more, and maintaining the temperature range for 100 seconds or less, the Ms point to 500 ° C. A secondary annealing step of heating to a temperature range and holding for 30 seconds or more in the temperature range.

  (2) The method for producing a high-strength steel sheet according to (1), wherein after the step (B), the annealed steel sheet is subjected to cold rolling with a total rolling reduction of 30% or more and less than 80%.

  (3) The high-strength steel plate according to (1) or (2), wherein after the step (A), the hot-rolled steel plate is subjected to cold rolling with a total rolling reduction of 30% or more and less than 80%. Manufacturing method.

(4) The chemical composition is mass%,
Ti: 0.005 to 0.20%,
Nb: 0.002-0.10%, and V: 0.005-0.50%,
The manufacturing method of the high strength steel plate in any one of said (1) to (3) containing 1 or more types selected from.

(5) The chemical composition is mass%,
Cr: 0.05% or more and less than 1.0%,
Mo: 0.02 to 0.50%,
Ni: 0.05-1.0%, and B: 0.0002-0.0050%,
The manufacturing method of the high strength steel plate in any one of said (1) to (4) containing 1 or more types selected from.

(6) The chemical composition is mass%,
Ca: 0.0005 to 0.020%,
Mg: 0.0005-0.020%, and REM: 0.0005-0.020%,
The manufacturing method of the high strength steel plate in any one of said (1) to (5) containing 1 or more types selected from.

(7) The chemical composition is mass%,
Cu: 0.05 to 1.0%
The manufacturing method of the high strength steel plate in any one of said (1) to (6) containing.

(8) The chemical composition is mass%,
Bi: 0.0005 to 0.020%
The manufacturing method of the high strength steel plate in any one of said (1) to (7) containing.

  According to the present invention, a steel sheet having high strength and excellent ductility and stretch flangeability can be obtained. Therefore, the high-strength steel plate manufactured by the method according to the present invention is suitable for use as a material for automobile members, machine structural members, building members and the like.

  The manufacturing method of the high strength steel plate which concerns on this invention comprises the following process (A)-(C). Hereinafter, each requirement of the present invention will be described in detail.

(A) Hot rolling step In step (A), a hot rolled steel sheet is obtained by subjecting a slab having a predetermined chemical composition to hot rolling to complete rolling in a temperature range of Ar _{3 to} 1100 ° C, 650 Wind in the temperature range below ℃. Each configuration will be described in more detail.

(A-1) Chemical composition of slab The reasons for limitation of each element are as follows. In the following description, “%” for the content means “% by mass”.

C: 0.04% or more and less than 0.50% C has an effect of increasing the strength of the steel sheet by solid solution strengthening and an effect of stabilizing retained austenite. If the C content is less than 0.04%, it becomes difficult to secure desired steel plate strength and retained austenite area ratio. On the other hand, if the C content is 0.50% or more, pearlite is preferentially generated, making it difficult to obtain the desired retained austenite area ratio. Therefore, the C content is 0.04% or more and less than 0.50%. The C content is preferably 0.06% or more, and more preferably 0.10% or more. Further, the C content is preferably 0.40% or less.

Si: 0.10% or more and less than 3.0% Si has an effect of increasing the strength of the steel sheet by solid solution strengthening and an effect of soundening the steel by deoxidation. Furthermore, it contributes to the improvement of ductility by delaying the precipitation of cementite and increasing the area ratio of retained austenite. If the Si content is less than 0.10%, it is difficult to obtain the effect by the above action. On the other hand, when the Si content is 3.0% or more, the surface properties and chemical conversion properties of the steel sheet deteriorate, and the ductility and weldability deteriorate significantly. Further, lead to significant increase in A ₃ transformation point, making it difficult to stably hot rolling. Therefore, the Si content is 0.10% or more and less than 3.0%.

  As will be described later, in the present invention, Si and sol. The total content of Al (Si + sol.Al) is important, but Si is sol. Solid solution strengthening ability is higher than Al. Therefore, when a higher strength is required, the Si content is preferably 0.50% or more, more preferably 0.80% or more, and further preferably 1.0% or more. Moreover, it is preferable that Si content is 2.5% or less.

Mn: 1.5 to 8.0%
Mn has the effect | action which raises the hardenability of steel and accelerates | stimulates the production | generation of a martensite. If the Mn content is less than 1.5%, it is difficult to ensure the target martensite amount. On the other hand, if the Mn content exceeds 8.0%, ferrite transformation is excessively suppressed, and it becomes difficult to secure the target amount of polygonal ferrite. Therefore, the Mn content is 1.5 to 8.0%. The Mn content is preferably 2.0% or more, and more preferably 2.3% or more. Moreover, it is preferable that Mn content is 6.0% or less.

P: 0.10% or less P is an element generally contained as an impurity, but is also an element having an effect of increasing strength by solid solution strengthening. Therefore, P may be positively included. However, P is an element that is easily segregated, and when its content exceeds 0.10%, the decrease in formability and toughness due to grain boundary segregation becomes significant. Therefore, the P content is 0.10% or less. The P content is preferably 0.050% or less, more preferably 0.030% or less, and even more preferably 0.020% or less. The lower limit of the P content is not particularly required, but is preferably 0.001% or more from the viewpoint of refining costs.

S: 0.030% or less S is an element contained as an impurity, and forms sulfide-based inclusions in the steel to lower the formability of the steel sheet. When the S content exceeds 0.030%, the moldability is significantly lowered. Therefore, the S content is 0.030% or less. The S content is preferably 0.010% or less, more preferably 0.005% or less, and still more preferably 0.001% or less. The lower limit of the S content is not particularly required, but is preferably 0.0001% or more from the viewpoint of suppressing an increase in refining cost.

sol. Al: 0.01 to 2.0%
Al has the effect | action which deoxidizes steel and makes a steel plate sound like Si. Furthermore, it contributes to the improvement of ductility by delaying the precipitation of cementite and increasing the area ratio of retained austenite. sol. If the Al content is less than 0.01%, it is difficult to obtain the effect of the above action. On the other hand, sol. If Al content exceeds 2.0%, inviting a significant increase in the A ₃ transformation point, making it difficult to stably hot rolling. Therefore, sol. The Al content is 0.01 to 2.0%. sol. The Al content is preferably 0.03% or more. Also, sol. The Al content is preferably 1.5% or less, and more preferably 1.0% or less.

N: 0.010% or less N is an element contained as an impurity, and has the effect of reducing the formability of the steel sheet. If the N content exceeds 0.010%, the moldability is significantly reduced. Therefore, the N content is 0.010% or less. The N content is preferably 0.0080% or less, and more preferably 0.0070% or less. The lower limit of the N content does not need to be specified, but it promotes precipitation of carbonitrides when considering the case where the steel structure is refined by containing one or more of Ti, Nb and V as described later. Therefore, the N content is preferably 0.0010% or more, and more preferably 0.0020% or more.

  In the steel plate of the present invention, in addition to the above elements, at least one selected from Ti, Nb, V, Cr, Mo, Ni, B, Ca, Mg, REM, Cu and Bi in the amounts shown below. These elements may be contained.

Ti: 0 to 0.20%
Nb: 0 to 0.10%
V: 0 to 0.50%
Ti, Nb, and V precipitate as carbides or nitrides in the steel, and have a function of refining the steel structure by the pinning effect. Therefore, you may contain 1 or more types selected from these elements. However, even if it contains excessively, the effect by the said effect | action will be saturated and it will become uneconomical. Therefore, the Ti content is 0.20% or less, the Nb content is 0.10% or less, and the V content is 0.50% or less. In order to more reliably obtain the effect of the above-described action of these elements, it is preferable to satisfy at least one of Ti: 0.005% or more, Nb: 0.002% or more, and V: 0.005% or more. .

Cr: 0% or more and less than 1.0% Mo: 0 to 0.50%
Ni: 0 to 1.0%
B: 0 to 0.0050%
Cr, Mo, Ni, and B have an effect of improving hardenability. Moreover, Mo has the effect | action which precipitates a carbide | carbonized_material in steel and raises an intensity | strength. Furthermore, Ni has the effect | action which suppresses effectively the grain boundary crack of the slab resulting from Cu, when containing Cu so that it may mention later. Therefore, you may contain 1 or more types selected from these elements.

  However, when the Cr content is 1.0% or more, the chemical conversion property is significantly lowered. Therefore, the Cr content is less than 1.0%. In order to more reliably obtain the effect of the above action, the Cr content is preferably 0.05% or more. On the other hand, if the Mo content exceeds 0.50%, the effect of the above action is saturated and disadvantageous in cost. Therefore, the Mo content is 0.50% or less. Preferably it is 0.20% or less. In order to more reliably obtain the effect of the above action, the Mo content is preferably set to 0.02% or more.

  Since Ni is an expensive element, a large amount is disadvantageous in terms of cost. Therefore, the Ni content is 1.0% or less. In order to more reliably obtain the effect of the above action, the Ni content is preferably 0.05% or more. On the other hand, when the B content exceeds 0.0050%, the moldability is significantly lowered. Therefore, the B content is 0.0050% or less. In order to more reliably obtain the effect of the above action, the B content is preferably set to 0.0002% or more.

Ca: 0 to 0.020%
Mg: 0 to 0.020%
REM: 0 to 0.020%
Ca, Mg, and REM have an effect of improving moldability by adjusting the shape of inclusions. Therefore, you may contain 1 or more types selected from these elements. However, if the content of these elements exceeds the above upper limit, the inclusions in the steel become excessive, and the formability may be lowered on the contrary. Therefore, the Ca content is 0.020% or less, the Mg content is 0.020% or less, and the REM content is 0.020% or less. Each element is preferably 0.010% or less, and more preferably 0.005% or less. In order to more reliably obtain the effect of the above action, it is preferable to contain 0.0005% or more of at least one of the above elements.

  Here, REM refers to a total of 17 elements of Sc, Y and lanthanoid, and the content of REM refers to the total content of these elements. In the case of a lanthanoid, it is industrially added in the form of misch metal.

Cu: 0 to 1.0%
Cu has the effect of increasing the strength by precipitation at a low temperature, so it may be contained in the steel. However, if the Cu content exceeds 1.0%, slab grain boundary cracking may occur. Therefore, the Cu content is 1.0% or less. The Cu content is preferably less than 0.5%, and more preferably less than 0.3%. In order to more reliably obtain the effect of the above action, the Cu content is preferably 0.05% or more.

Bi: 0 to 0.020%
Bi has the effect of improving the formability by refining the solidified structure, so it may be contained in the steel. However, if the Bi content exceeds 0.020%, the effect of the above action is saturated, which is disadvantageous in terms of cost. Therefore, the Bi content is 0.020% or less. The Bi content is preferably 0.010% or less. In order to more reliably obtain the effect of the above action, the Bi content is preferably set to 0.0005% or more.

0.5 ≦ Si + sol. Al ≦ 3.0 (i)
However, each element symbol in the above formula (i) represents the content (% by mass) of each element contained in the steel sheet.
As described above, both Si and Al have the effect of suppressing the precipitation of cementite and increasing the retained austenite area ratio and improving the ductility. Therefore, in the present invention, Si and sol. The total content (Si + sol.Al) with Al is specified.

Si + sol. When the value of Al is less than 0.5, the above-described effect is insufficient, so that a desired retained austenite area ratio cannot be obtained and ductility deteriorates. On the other hand, Si + sol. When the value of Al is more than 3.0, inviting a significant increase in the A ₃ transformation point, making it difficult to stably hot rolling. Therefore, it is necessary to satisfy the above formula (i). Si + sol. The value of Al is preferably 1.0 or more, and more preferably 1.2 or more. In addition, Si + sol. The value of Al is preferably 2.5 or less, and more preferably 2.2 or less.

  In the chemical composition of the steel sheet of the present invention, the balance is Fe and impurities.

  "Impurity" is a component that is mixed due to various factors in raw materials such as ores and scraps and manufacturing processes when industrially manufacturing steel materials, and is allowed within a range that does not adversely affect the present invention. Means things.

(A-2) Hot rolling conditions Slab heating temperature: 1350 ° C. or less The temperature of the slab used for hot rolling is preferably 1350 ° C. or less, more preferably 1280 ° C. or less from the viewpoint of suppressing scale loss. preferable. The lower limit of the temperature of the slab to be subjected to hot rolling is not particularly limited as long as it is a temperature at which hot rolling can be completed at Ar ₃ points or more as described later.

Rolling completion temperature: Ar ₃ points to 1100 ° C
Hot rolling is completed in a temperature range of Ar ₃ or higher in order to refine the metal structure of the hot-rolled steel sheet by transforming austenite after completion of rolling. When the rolling completion temperature is less than Ar ₃ point, ferrite transformation occurs during hot rolling, and a coarse low-temperature transformation phase extending in the rolling direction is generated in the metal structure of the hot-rolled steel sheet. As a result, the metal structure after annealing becomes coarse, and the ductility and stretch flangeability tend to deteriorate. For this reason, the completion temperature of hot rolling needs to be Ar ₃ points or more.

  On the other hand, when the temperature at the completion of rolling exceeds 1100 ° C., the metal structure of the hot-rolled steel sheet becomes coarse, the metal structure after annealing becomes coarse, and the ductility and stretch flangeability tend to deteriorate. For this reason, the completion temperature of hot rolling needs to be 1100 degrees C or less. The completion temperature is preferably 1050 ° C. or lower.

  In addition, when hot rolling consists of rough rolling and finish rolling, in order to complete finish rolling at the said temperature, you may heat a rough rolling material between rough rolling and finish rolling. At this time, it is desirable to suppress the fluctuation of the temperature over the entire length of the rough rolled material at the start of finish rolling to 140 ° C. or less by heating so that the rear end of the rough rolled material is higher than the tip. Thereby, the uniformity of the product characteristic in a coil improves.

  The heating method of the rough rolled material may be performed using a known means. For example, a solenoid induction heating device is provided between the rough rolling mill and the finish rolling mill, and the heating temperature rise is controlled based on the temperature distribution in the longitudinal direction of the rough rolled material on the upstream side of the induction heating device. May be.

  Moreover, it is preferable to use a lever mill or a tandem mill for hot rolling as multipass rolling. In particular, from the viewpoint of industrial productivity, at least the final several stages are more preferably rolled using a tandem mill.

Primary cooling after completion of rolling: Cooling is started within 10 seconds after completion of rolling, and cooling is performed at a cooling rate of 5 ° C./second or more. When the temperature is less than 5 ° C., the metal structure of the hot-rolled steel sheet becomes coarse, the metal structure after annealing becomes coarse, and the ductility and stretch flangeability tend to deteriorate. For this reason, the primary cooling after the completion of rolling is preferably started within 10 seconds and cooled at a cooling rate of 5 ° C./second or more.

Winding temperature: 650 ° C. or less The annealing at the two-phase region temperature (primary annealing) of ferrite and austenite performed after hot rolling promotes the distribution of Mn between ferrite and austenite, followed by annealing (two By subsequent annealing, it becomes possible to control the relationship between the area ratio of polygonal ferrite, the Mn concentration in martensite, and the Mn concentration in polygonal ferrite within a desired range. In order to obtain the effect, the coiling temperature after hot rolling needs to be 650 ° C. or less. When the coiling temperature exceeds 650 ° C., pearlite is easily generated, and Mn distribution proceeds between ferrite and pearlite, and a structure suitable for ductility and stretch flangeability cannot be obtained. The winding temperature is preferably less than 400 ° C, and more preferably less than 300 ° C.

(B) Primary annealing step The hot-rolled steel sheet obtained in the step (A) is annealed at a two-phase temperature range of ferrite and austenite. This annealing is called “primary annealing” in the present invention. By promoting the distribution of Mn between ferrite and austenite by primary annealing, it becomes easy to obtain a metal structure suitable for ductility and stretch flangeability. The primary annealing conditions will be described in detail below.

Primary annealing temperature: (Ac ₃ points-50 ° C) to (Ac ₃ points-2 ° C)
The primary annealing temperature is (Ac ₃ points−50 ° C.) to (Ac ₃ points−2 ° C.). By annealing at a temperature in this range, it becomes possible to control the relationship between the area ratio and average particle diameter of polygonal ferrite, the Mn concentration in martensite and the Mn concentration in polygonal ferrite to a desired range. . If the primary annealing temperature is less than (Ac ₃ point-50 ° C.), coarse polygonal ferrite is likely to be generated, and stretch flangeability deteriorates. On the other hand, when the primary annealing temperature exceeds (Ac ₃ point -2 ° C), it becomes difficult to secure a desired amount of polygonal ferrite, and ductility deteriorates.

Primary annealing holding time: satisfies the following formula (ii) The primary annealing holding time needs to satisfy the following formula (ii) in relation to the above-mentioned primary annealing temperature.
1.4 × 10 ⁻⁸ × exp {26500 / (T + 273)} ≦ t ≦ 4.0 × 10 ⁵ (ii)
However, the meaning of each symbol in the above formula (ii) is as follows.
t: Primary annealing holding time (seconds)
T: Primary annealing temperature (° C)

Since the diffusion rate of Mn is very slow, the Mn concentration in the martensite and the Mn in the polygonal ferrite are promoted by maintaining Mn distribution from the ferrite to the austenite by maintaining the primary annealing temperature for a predetermined time. It becomes possible to control the relationship with the density within a desired range. When the holding time is less than the left side of the formula (ii) [1.4 × 10 ⁻⁸ × exp {6500 / (T + 273)}], the distribution of Mn is insufficient, so the Mn concentration in martensite and the polygonal ferrite The ratio of the Mn concentration to the desired value does not become a desired value, and ductility deteriorates. On the other hand, since the Mn concentration ratio approaches an equilibrium state when it is held for a long time, even if annealing exceeding 4.0 × 10 ⁵ seconds is performed, the heat treatment cost is increased.

(C) Secondary annealing step The annealed steel sheet obtained in the step (B) is subjected to treatments such as descaling and degreasing according to known methods as necessary, and then annealed. This annealing is called “secondary annealing” in the present invention. By performing secondary annealing, martensite and retained austenite are generated. Thereby, it becomes easy to obtain a metal structure suitable for ductility and stretch flangeability. The secondary annealing conditions will be described in detail below.

Secondary annealing temperature: (Ac ₃ points−40 ° C.) or more and less than (Ac ₃ points + 100 ° C.) The secondary annealing temperature needs to be (Ac ₃ points−40 ° C.) or more. This is because a main phase is martensite and a metal structure containing residual austenite in the second phase is obtained. In order to increase the area ratio of martensite and improve stretch flangeability, the secondary annealing temperature is preferably set to a temperature exceeding (Ac ₃ point−20 ° C.), and the temperature exceeding Ac ₃ point. Is more preferable. However, if the secondary annealing temperature becomes too high, austenite becomes excessively coarse, and the Mn distribution promoted by the primary annealing decreases due to diffusion, and ductility and stretch flangeability deteriorate. For this reason, the secondary annealing temperature needs to be less than (Ac ₃ points + 100 ° C.). The secondary annealing temperature is preferably less than (Ac ₃ points + 50 ° C.), and more preferably less than (Ac ₃ points + 20 ° C.).

Secondary annealing holding time: less than 150 seconds The lower limit of the holding time at the secondary annealing temperature is not particularly limited, but in order to obtain stable mechanical properties, it is preferable that the time exceeds 15 seconds, and 60 seconds. More preferably, the time is over. On the other hand, if the holding time is too long, diffusion of Mn distributed by primary annealing occurs, and ductility and stretch flangeability are likely to deteriorate. For this reason, the holding time is preferably less than 150 seconds, and more preferably less than 120 seconds.

  In the heating process in the secondary annealing, in order to suppress the diffusion of Mn distributed in the primary annealing, the average heating rate is preferably 5 ° C./second or more, more preferably 20 ° C./second or more, and 100 ° C. / Second or more is more preferable.

  In the cooling process after soaking of the secondary annealing, in order to promote the formation of fine polygonal ferrite and improve the ductility, the cooling is performed at a cooling rate of less than 10 ° C / sec. Preferably it is done. The cooling rate after soaking is preferably less than 5 ° C./second, more preferably less than 3 ° C./second, and even more preferably less than 2 ° C./second. In addition, since the Mn distribution is generated in the steel sheet by the primary annealing, the polygonal ferrite is preferentially generated from a portion having a low Mn concentration. Thereby, the relationship between the polygonal ferrite area ratio suitable for ductility and stretch flangeability and the Mn concentration in martensite and the Mn concentration in polygonal ferrite can be easily obtained.

  Moreover, in order to obtain the metal structure which has a martensite as a main phase, the average cooling rate in the temperature range of 650-500 degreeC shall be 15 degrees C / second or more. The average cooling rate in the temperature range of 650 to 450 ° C. is preferably 15 ° C./second or more. Since the martensite area ratio increases as the cooling rate increases, the average cooling rate is more preferably higher than 30 ° C./second, and more preferably higher than 50 ° C./second. On the other hand, if the cooling rate is too high, the shape of the steel sheet is impaired, so the cooling rate in the temperature range of 650 to 500 ° C. is preferably 200 ° C./second or less, more preferably less than 150 ° C./second. Preferably, the temperature is less than 130 ° C./second.

  Next, in order to generate martensite, it is necessary to hold for 100 seconds or less in a temperature range of (Ms point−200 ° C.) to (Ms point−20 ° C.). As a result, a desired martensite area ratio is obtained, and part of the martensite area remains as untransformed austenite, and a desired retained austenite area ratio is obtained by subsequent heat treatment. When the holding temperature is lower than (Ms point−200 ° C.), the ratio of untransformed austenite is small, and a desired retained austenite area ratio cannot be obtained. On the other hand, if it exceeds (Ms-20 ° C.), the desired martensite area ratio cannot be obtained. Further, if the temperature is maintained for more than 100 seconds in this temperature range, cementite precipitates due to tempering, and stretch flangeability deteriorates.

  Furthermore, in order to obtain retained austenite, it is necessary to heat to a temperature range of Ms point to 500 ° C. and hold in the temperature range for 30 seconds or more. In order to improve the stability of retained austenite and improve ductility and stretch flangeability, the holding temperature range is preferably 475 ° C. to (Ms point + 20 ° C.), and 450 ° C. to (Ms point + 40 ° C.). ) Is more preferable, and 430 ° C. to (Ms point + 60 ° C.) is further preferable. Further, since the stability of retained austenite increases as the holding time is increased, the holding time is preferably 60 seconds or more, more preferably 120 seconds or more, and more than 300 seconds. Further preferred.

The Ms point is calculated from the element content using the following formula (iii).
Ms point (° C.) = 561-407 × C-7.3 × Si-37.8 × Mn-20.5 × Cu-19.5 × Ni-19.8 × Cr-4.5 × Mo (Iii)
However, each element symbol in the above formula (iii) represents the content (% by mass) of each element contained in the steel sheet.

(D) Other steps (D-1) Casting step No particular limitation is imposed on the method for producing a slab used as a raw material for hot rolling in the step (A). The steel having the above-mentioned chemical composition is made into a steel ingot by a continuous casting method after being melted by a known means, or by a method such as a method of performing a block rolling after making a steel ingot by an arbitrary casting method. It is taken as a piece. In the continuous casting process, in order to suppress the occurrence of surface defects due to inclusions, it is preferable to cause an external additional flow such as electromagnetic stirring in the molten steel in the mold.

  The steel ingot or steel slab may be reheated once it has been cooled and subjected to hot rolling. The steel ingot in the high temperature state after continuous casting or the steel slab in the high temperature state after partial rolling is used as it is. Alternatively, it may be subjected to hot rolling by keeping it warm or performing auxiliary heating. In the present invention, such steel ingots and steel pieces are collectively referred to as slabs.

(D-2) Cold rolling step Cold pressure ratio: 30% or more and less than 80% For the annealed steel plate after the step (B) and / or the hot-rolled steel plate after the step (A), it is cold according to a conventional method. Rolling may be performed. Moreover, you may descal to an annealed steel plate and / or a hot-rolled steel plate by pickling before cold rolling. In cold rolling, in order to promote recrystallization and make the metal structure after cold rolling and annealing uniform and further improve stretch flangeability, the cold rolling ratio (total rolling reduction in cold rolling) is 30% or more. It is preferable that The cold pressure ratio is more preferably 40% or more. This further refines the metal structure after annealing, improves the texture, and further improves ductility and stretch flangeability. From this viewpoint, the cold pressure ratio is more preferably a value exceeding 50%, and particularly preferably a value exceeding 60%. On the other hand, if the cold pressure ratio is too high, the rolling load increases and rolling becomes difficult, so the cold pressure ratio is preferably less than 80%, and more preferably less than 70%.

(D-3) Plating step When producing an electroplated steel sheet, the annealed steel sheet produced by the above-described method is subjected to a known pretreatment for surface cleaning and adjustment as necessary, Electroplating may be performed according to a conventional method, and the chemical composition and the amount of deposition of the plating film are not limited. Examples of types of electroplating include electrogalvanizing and electro-Zn-Ni alloy plating.

  When manufacturing a hot-dip plated steel sheet, in the cooling process of the step (C), after holding for 30 seconds or more in a temperature range of 500 ° C. to Ms point, the steel sheet is heated as necessary and then put into a plating bath. Immerse and apply hot-dip plating. In order to improve the stability of retained austenite and improve ductility and stretch flangeability, the holding temperature range is preferably 475 ° C. to (Ms point + 20 ° C.), and 450 ° C. to (Ms point + 40 ° C.). It is more preferable to set the temperature to 430 ° C. to (Ms point + 60 ° C.).

  Moreover, since the stability of retained austenite increases as the holding time in the temperature range of 500 ° C. to Ms is increased, the holding time is preferably 60 seconds or more, more preferably 120 seconds or more, 300 More preferably, the time exceeds 2 seconds. The alloying treatment may be performed by reheating after hot dipping. The chemical composition and the amount of adhesion of the plating film are not limited. Examples of hot dip plating include hot dip galvanizing, alloyed hot dip galvanizing, hot dip aluminum plating, hot dip Zn-Al alloy plating, hot dip Zn-Al-Mg alloy plating, hot dip Zn-Al-Mg-Si alloy plating, etc. Is done.

  In order to further improve the corrosion resistance, the plated steel sheet may be subjected to an appropriate chemical conversion treatment after plating. The chemical conversion treatment is preferably carried out using a non-chromium type chemical conversion treatment solution (for example, silicate type, phosphate type, etc.) instead of the conventional chromate treatment.

  The annealed steel plate and the plated steel plate thus obtained may be subjected to temper rolling according to a conventional method. However, if the elongation rate of the temper rolling is high, the ductility is deteriorated. Therefore, the elongation rate of the temper rolling is preferably 1.0% or less, and more preferably 0.5% or less.

  The high-strength steel sheet produced by the method according to the present invention has a main phase of martensite and a metal structure containing polygonal ferrite and retained austenite in the second phase. The metal structure of the steel sheet according to the present invention will be described below.

Martensite area ratio: 60.0-95.0%
Martensite is a hard and homogeneous structure, and is a structure suitable for combining high strength and excellent stretch flangeability. Therefore, in the steel plate according to the present invention, the main phase needs to be martensite. In the present invention, martensite being the main phase means that the area ratio of martensite is 60.0% or more.

  The martensite area ratio is not particularly limited, but if it is less than 60.0%, it is difficult to obtain desired strength and stretch flangeability. On the other hand, if the area ratio of martensite exceeds 95.0%, the ductility may be significantly reduced. Therefore, the area ratio of martensite is preferably 60.0 to 95.0%. The area ratio of martensite is more preferably 70.0% or more. In addition, the martensite in this invention is a general term for the tempered martensite other than what is called a fresh martensite produced | generated by a shearing mechanism without diffusion.

  In the steel sheet according to the present invention, the second phase contains polygonal ferrite and retained austenite. There are no particular restrictions on the area ratio and grain size of polygonal ferrite and retained austenite, but the following ranges are preferred.

Polygonal ferrite area ratio: 2.0-25.0%
In order to improve ductility by including soft polygonal ferrite, the area ratio of polygonal ferrite is preferably set to 2.0 to 25.0%. If the area ratio of polygonal ferrite is less than 2.0%, it is difficult to obtain the effect of improving ductility. On the other hand, if it exceeds 25.0%, not only the stretch flangeability is deteriorated, but also it is difficult to secure a desired strength. The area ratio of polygonal ferrite is more preferably 5.0% or more, and further preferably 6.0% or more. The area ratio is more preferably 20.0% or less, and further preferably 15.0% or less.

Area ratio of retained austenite: 3.0 to 35.0%
Residual austenite has the effect of increasing ductility by transformation induced plasticity (TRIP). When the retained austenite area ratio is less than 3.0%, it is difficult to obtain the effect by the above action. On the other hand, if the area ratio of retained austenite exceeds 35.0%, the stretch flangeability may be deteriorated by hard martensite generated by the processing-induced transformation. Accordingly, the retained austenite area ratio is preferably 3.0 to 35.0%. The retained austenite area ratio is more preferably 4.0% or more, and still more preferably 6.0% or more.

  In addition, there exists a method by X-ray diffraction, an electron beam backscattering diffraction image (EBSP) analysis, a magnetic measurement etc. in the determination method of a retained austenite, and a fixed value may differ with methods. The area ratio of retained austenite specified in the present invention is a value measured by X-ray diffraction.

  The steel sheet according to the present invention may contain cementite, pearlite, bainitic ferrite, and the like as the balance in addition to the above-described structure. If the total area ratio of the remaining structure excluding martensite, polygonal ferrite and retained austenite exceeds 15.0%, stretch flangeability may be deteriorated. From the viewpoint of moldability, the area ratio of the remainder is preferably 15.0% or less. The area ratio of the remainder is more preferably 10.0% or less, and even more preferably 6.0% or less.

Polygonal ferrite average particle size: 0.3-10.0 μm
When the average particle size of polygonal ferrite is less than 0.3 μm, the ductility may be deteriorated. On the other hand, if the average particle size exceeds 10.0 μm, coarse voids may be generated at the interface between polygonal ferrite and martensite, and stretch flangeability may deteriorate. From the viewpoint of reducing the hardness difference from martensite by strengthening the fine particles and improving stretch flangeability, the average particle size of polygonal ferrite is preferably 10.0 μm or less.

  The average particle size of polygonal ferrite is more preferably 0.8 μm or more, and further preferably 1.2 μm or more. The average particle size is more preferably 7.0 μm or less, and further preferably 5.0 μm or less. In addition, the average particle diameter of polygonal ferrite in the present invention is an equivalent circle diameter obtained by image analysis using a scanning electron microscope (SEM) observation image and an EBSP analysis result.

  Further, the average aspect ratio of polygonal ferrite is preferably 3.0 or less, more preferably 2.5 or less, from the viewpoint of reducing anisotropy and improving stretch flangeability. The average aspect ratio of polygonal ferrite is a value represented by (major axis length) / (minor axis length) obtained by ellipse approximation from image analysis using SEM observation images and EBSP analysis results. It is.

Average particle diameter of retained austenite: 1.0 μm or less When the average particle diameter of retained austenite exceeds 1.0 μm, stretch flangeability may deteriorate due to martensite generated by the processing-induced transformation. Therefore, the average particle size of retained austenite is preferably 1.0 μm or less. The average particle size of the retained austenite is more preferably 0.8 μm or less, and further preferably 0.6 μm or less.

0.25 <[Mn] _PF / [Mn] _M <0.70 (iv)
However, the meaning of each symbol in the above formula (iv) is as follows.
[Mn] _PF : Average Mn concentration (% by mass) in polygonal ferrite
[Mn] _M : Average Mn concentration (mass%) in martensite
In order to control the hardness difference between martensite and polygonal ferrite so that the ductility and stretch flangeability are combined at a high level, the Mn concentration in martensite and the Mn concentration in polygonal ferrite are expressed by the above formula (iv). It is preferable to satisfy.

  When the average Mn concentration in polygonal ferrite is 0.70 times or more than the average Mn concentration in martensite, the solid solution strengthening amount of polygonal ferrite by Mn is large, and it is difficult to obtain desired ductility. On the other hand, when the average Mn concentration in polygonal ferrite is 0.25 times or less than the average Mn concentration in martensite, the hardness difference between martensite and polygonal ferrite is large, so coarse voids are generated during deformation. It is easy to cause stretch flangeability.

  The metal structure is identified and the area ratio is calculated by the following method. First, a vertical cross section in the rolling direction of a steel sheet is mirror-polished and then subjected to nital corrosion, and a metal structure is identified from structure observation using an optical microscope or SEM. Next, the area ratio of polygonal ferrite at a position at a depth of ¼ of the plate thickness from the steel plate surface is calculated from the EBSP analysis. Moreover, the residual austenite area ratio is calculated | required by X-ray-diffraction measurement using the sample which faced from the rolling surface normal direction to the 1/4 depth of plate | board thickness.

  Furthermore, using a sample that has undergone repeller corrosion, an image of a rolling direction vertical section at a quarter depth of the sheet thickness from the surface of the steel sheet in a rolling direction of 200 μm × rolling surface normal direction of 50 μm was photographed with an optical microscope, and commercially available image processing software The total area ratio of retained austenite and martensite is calculated by binarization using “Image-Pro”. A value obtained by subtracting the residual austenite area ratio determined by X-ray diffraction measurement from the total area ratio of residual austenite and martensite determined by the repeller corrosion is defined as a martensite area ratio.

  Then, a value obtained by subtracting the total area ratio of martensite, polygonal ferrite and retained austenite obtained above from 100% is defined as the area ratio of the remaining structure. Moreover, the average particle diameters of polygonal ferrite and retained austenite are calculated from EBSP analysis and transmission electron microscope (TEM) observation of a thin film test piece taken from the steel sheet surface at a depth of 1/4 of the plate thickness.

  The Mn concentration in polygonal ferrite and martensite is determined by the following method using an electron beam microanalyzer (FE-EPMA) equipped with a field emission electron gun. First, mapping analysis of Mn concentration is performed with FE-EPMA at an interval of 0.1 μm in a 50 μm × 50 μm region at a depth of 1/4 of the plate thickness from the surface of the steel plate. Next, the metal structure of the same visual field is identified from the EBSP analysis by the method described above. For the identified martensite and polygonal ferrite, the average value of the Mn concentrations at any 10 points is calculated and used as the Mn concentrations of martensite and polygonal ferrite.

  EXAMPLES Hereinafter, although an Example demonstrates this invention more concretely, this invention is not limited to these Examples.

  A 180 kg steel ingot having the chemical composition shown in Table 1 was melted in a high-frequency vacuum melting furnace and made into a 30 mm thick steel piece by hot forging. This steel slab was hot-rolled with a test small tandem mill under the conditions shown in Table 2 to obtain a hot-rolled steel sheet having a thickness of 2 to 4 mm. The hot-rolled steel sheet was heat-treated at various primary annealing temperatures shown in Table 2 for a predetermined time, and then cooled to room temperature.

  Subsequently, the obtained primary annealed steel sheet was heated to various secondary annealing temperatures shown in Table 2 using a continuous annealing simulator and held for a predetermined time. Then, after cooling under various conditions shown in Table 2, and holding at that temperature for a predetermined time, the temperature was raised again to the temperature shown in Table 2, held at that temperature for 330 seconds, then cooled to room temperature and annealed steel sheet. Obtained.

  In addition, about some of said hot-rolled steel plates and / or primary annealing steel plates, it annealed after performing pickling and cold rolling.

  About the obtained annealed steel plate, the vertical cross section of the steel plate in the rolling direction was mirror-polished and corroded with a nital corrosive solution or a repeller corrosive solution, and then the structure was observed using an optical microscope or SEM. Furthermore, the crystal orientation was measured and analyzed by the EBSP method using a sample prepared by electrolytic polishing after mirror polishing. Further, a thin piece for TEM observation was taken from the steel sheet surface from a 1/4 depth position of the plate thickness, and the vicinity opened by the twin jet electrolysis method was observed by TEM. Furthermore, the structure of the same visual field was analyzed by the FE-EPMA and EBSP methods, and the Mn concentration in martensite and polygonal ferrite was determined.

  As mechanical properties, tensile properties and stretch flangeability were evaluated. As for the tensile properties, a tensile test was performed according to JIS Z 2241 (2011), and tensile strength (TS) and total elongation (El) were measured. For stretch flangeability, a hole expansion test was performed in accordance with JIS Z 2256 (2010) to obtain a hole expansion ratio (λ).

  Table 3 shows the metal structure and mechanical properties of the obtained steel sheet. In the present invention, a steel sheet having a tensile strength of 980 MPa or more, a TS × EL value of 16000 MPa ·% or more, and a TS × λ value of 50000 MPa ·% or more has high tensile strength and strength. -It shall be determined that the ductility balance and strength-stretch flangeability balance are excellent.

  With reference to Tables 1 to 3, Test Nos. 1 to 20 which are examples of the present invention have high tensile strength (TS), excellent strength-ductility balance (TS × El), and excellent strength-stretch flange balance. (TS × λ). On the other hand, in the test numbers 21 to 33 which are comparative examples manufactured by a method not satisfying the provisions of the present invention, either TS × El or TS × λ characteristics are inferior.

  According to the present invention, a steel sheet having high strength and excellent ductility and stretch flangeability can be obtained. Therefore, the high-strength steel plate manufactured by the method according to the present invention is suitable for use as a material for automobile members, machine structural members, building members and the like.

Claims (8)

The main phase is martensite and the second phase is a method for producing a high-strength steel sheet having a metal structure containing polygonal ferrite and retained austenite,
The manufacturing method of a high strength steel plate provided with the following process (A)-(C).
(A) In mass%,
C: 0.04% or more and less than 0.50%,
Si: 0.10% or more and less than 3.0%,
Mn: 1.5 to 8.0%,
P: 0.10% or less,
S: 0.030% or less,
sol. Al: 0.01 to 2.0%,
N: 0.010% or less,
Ti: 0 to 0.20%,
Nb: 0 to 0.10%,
V: 0 to 0.50%,
Cr: 0% or more and less than 1.0%,
Mo: 0 to 0.50%,
Ni: 0 to 1.0%,
B: 0 to 0.0050%,
Ca: 0 to 0.020%,
Mg: 0 to 0.020%,
REM: 0 to 0.020%,
Cu: 0 to 1.0%
Bi: 0 to 0.020%,
Balance: Fe and impurities,
For a slab having a chemical composition satisfying the following formula (i):
A hot rolling step in which hot rolling is performed in a temperature range of Ar _{3 to} 1100 ° C. to form a hot-rolled steel sheet, and winding is performed in a temperature range of 650 ° C. or lower.
0.5 ≦ Si + sol. Al ≦ 3.0 (i)
However, each element symbol in the above formula (i) represents the content (% by mass) of each element contained in the steel sheet.
(B) Primary holding the hot-rolled steel sheet obtained in the step (A) in a temperature range of (Ac ₃ points-50 ° C.) to (Ac ₃ points-2 ° C.) for a time satisfying the following formula (ii). Annealing process.
1.4 × 10 ⁻⁸ × exp {26500 / (T + 273)} ≦ t ≦ 4.0 × 10 ⁵ (ii)
However, the meaning of each symbol in the above formula (ii) is as follows.
t: Primary annealing holding time (seconds)
T: Primary annealing temperature (° C)
(C) After holding the annealed steel sheet obtained in the step (B) in a temperature range of (Ac ₃ points−40 ° C.) or more and less than (Ac ₃ points + 100 ° C.), the average in the temperature range of 650 to 500 ° C. After cooling to a temperature range of (Ms−200 ° C.) to (Ms−20 ° C.) so that the cooling rate is 15 ° C./second or more, and maintaining the temperature range for 100 seconds or less, the Ms point to 500 ° C. A secondary annealing step of heating to a temperature range and holding for 30 seconds or more in the temperature range.   The method for producing a high-strength steel sheet according to claim 1, wherein after the step (B), the annealed steel sheet is subjected to cold rolling with a total rolling reduction of 30% or more and less than 80%.   The manufacturing method of the high strength steel plate of Claim 1 or Claim 2 which performs the cold rolling whose total reduction rate is 30% or more and less than 80% with respect to the said hot-rolled steel plate after the said process (A). The chemical composition is mass%,
Ti: 0.005 to 0.20%,
Nb: 0.002-0.10%, and V: 0.005-0.50%,
The manufacturing method of the high strength steel plate in any one of Claim 1 to 3 containing 1 or more types selected from. The chemical composition is mass%,
Cr: 0.05% or more and less than 1.0%,
Mo: 0.02 to 0.50%,
Ni: 0.05-1.0%, and B: 0.0002-0.0050%,
The manufacturing method of the high strength steel plate in any one of Claim 1 to 4 containing 1 or more types selected from. The chemical composition is mass%,
Ca: 0.0005 to 0.020%,
Mg: 0.0005-0.020%, and REM: 0.0005-0.020%,
The manufacturing method of the high strength steel plate in any one of Claim 1-5 containing 1 or more types selected from. The chemical composition is mass%,
Cu: 0.05 to 1.0%
The manufacturing method of the high strength steel plate in any one of Claim 1- Claim 6 containing this. The chemical composition is mass%,
Bi: 0.0005 to 0.020%
The manufacturing method of the high-strength steel plate in any one of Claim 1 to 7 containing this.